[go: up one dir, main page]

US20180127844A1 - Method for Manufacturing a Component Made of Austenitic Steel - Google Patents

Method for Manufacturing a Component Made of Austenitic Steel Download PDF

Info

Publication number
US20180127844A1
US20180127844A1 US15/575,541 US201615575541A US2018127844A1 US 20180127844 A1 US20180127844 A1 US 20180127844A1 US 201615575541 A US201615575541 A US 201615575541A US 2018127844 A1 US2018127844 A1 US 2018127844A1
Authority
US
United States
Prior art keywords
component
deformation
deformed
steel
austenitic steel
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Granted
Application number
US15/575,541
Other versions
US10774395B2 (en
Inventor
Thomas Fröhlich
Stefan Lindner
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Outokumpu Oyj
Original Assignee
Outokumpu Oyj
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Outokumpu Oyj filed Critical Outokumpu Oyj
Publication of US20180127844A1 publication Critical patent/US20180127844A1/en
Assigned to OUTOKUMPU OYJ reassignment OUTOKUMPU OYJ ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: Fröhlich, Thomas, LINDNER, STEFAN
Application granted granted Critical
Publication of US10774395B2 publication Critical patent/US10774395B2/en
Expired - Fee Related legal-status Critical Current
Adjusted expiration legal-status Critical

Links

Images

Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B62—LAND VEHICLES FOR TRAVELLING OTHERWISE THAN ON RAILS
    • B62D—MOTOR VEHICLES; TRAILERS
    • B62D25/00—Superstructure or monocoque structure sub-units; Parts or details thereof not otherwise provided for
    • B62D25/04—Door pillars ; windshield pillars
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B62—LAND VEHICLES FOR TRAVELLING OTHERWISE THAN ON RAILS
    • B62D—MOTOR VEHICLES; TRAILERS
    • B62D29/00—Superstructures, understructures, or sub-units thereof, characterised by the material thereof
    • B62D29/007—Superstructures, understructures, or sub-units thereof, characterised by the material thereof predominantly of special steel or specially treated steel, e.g. stainless steel or locally surface hardened steel
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite

Definitions

  • the present invention relates to a method for manufacturing a component made of austenitic manganese alloyed steel using the TWIP (Twinning-Induced Plasticity) effect of the steel to achieve a component having an essentially same thickness for the whole component but having regions with different mechanical property values.
  • TWIP Twin-Induced Plasticity
  • the US publication 2013048150 describes a method for producing a workpiece having properties which are adjustable across a wall or a strip thickness by a special decarburizing annealing process, using the TRIP hardening effect of a high-manganese alloyed steel.
  • the WO publication 2014180456 describes a method for producing with only one material, austenitic lightweight construction steel, a component which has different material properties.
  • the core is reached by a specific forming, where the austenitic lightweight construction steel has a temperature-dependent transformation induced plasticity (TRIP) and/or twinning induced plasticity effect (TWIP) during transformation
  • TRIP temperature-dependent transformation induced plasticity
  • TWIP twinning induced plasticity effect
  • a gryogenic treatment is described also in the US publication 2014328715 in a method for producing a TWIP and nano twinned austenitic stainless steel containing less than 0.018 wt % C, 0.25-0.75 wt % Si, 1.5-2 wt % Mn, 17.80-19.60 wt % Cr, 24.00-25.25 wt % Ni, 3.75-4.85 wt % Mo, 1.26-2.78 wt % Cu, 0.04-0.15 wt % N the rest being Fe and unavoidable impurities.
  • the TWIP (Twinning-Induced Plasticity) effect depends on the chemical composition, austenitic microstructure hardening effect and the stacking fault energy (20-30 mJ/m 2 ).
  • the twinning causes a high value of instantaneous hardening rate when the microstructure becomes finer and finer.
  • the resultant twin boundaries act like grain boundaries and strengthen the steel.
  • the hardening rate value increases to a value of 0.4 at an approximate engineering strain of 30% and then remains constant until both the uniform elongation and the total elongation reach 50%.
  • the method for manufacturing of steel grades having the TWIP effect with different chemical compositions is also described for instance in the CN publication 103556052, in the CN publication 102312158, in the EP publication 2649214, in the KR publication 20100028310 and in the KR publication 20100009222.
  • the WO publication 2014/097184 relates to a use of the austenitic stainless steel with TWIP effect containing in weight % 0.01-0.50% C, 0.001-0.5% Si, 6-12% Mn, 11-20% Cr, 0.01-6.0% Ni, 0.01-2.0% Mo, 0.01-2.0 Co, 0.01-6.0% Cu, 0.11-0.50% N, 0.001-0.5% Nb, 0.001-2.0% Al, the rest being Fe and unavoidable impurities, for manufacturing automobile components with complex geometry for energy absorption, structural reinforcements and/or applications by deep drawing wherein corrosion resistance is requested.
  • the object of the present invention is to eliminate drawbacks of the prior art and to establish a method for manufacturing a component made of austenitic manganese alloyed steel using the TWIP effect by forming of the semi-manufactured product having essentially the same thickness to a component with regions having different mechanical property values.
  • the essential features of the present invention are enlisted in the appended claims.
  • a workpiece made of manganese alloyed steel is deformed using the TWIP (Twinning-Induced Plasticity) effect of the steel to achieve a component with essentially the same thickness, the range of the uniform thickness being 0.5-2.0 millimeter but which component has at least two regions having different mechanical property values.
  • the mechanical property values desired for each region are dependent on the deformation level or the deformation degree which is performed for the workpiece. Therefore, according to the invention it is possible to achieve regions in the component which regions have different behavior in point of for instance stiffness, energy absorption, crash resistance.
  • the workpiece to be deformed in the method of the present invention is made of austenitic steel having stacking fault energy at the range of 18-30 mJ/m 2 .
  • the manganese content of the steel is 10-25 weight %, preferably 15-20 weight %.
  • the steel advantageously contains interstitial disengaged nitrogen and carbon atoms so that the sum of the carbon content and the nitrogen content (C+N) is at least 0.4 weight %, but less than 1.2 weight %, and the steel advantageously can also contain more than 10.5 weight % chromium, being thus an austenitic stainless steel.
  • the steel contains essential contents of at least one ferrite former, such as chromium
  • a compensation with the contents of the austenite formers, such as manganese, carbon, nitrogen, nickel or copper will be done in order to have a balanced and sole content of austenite in the microstructure of the steel.
  • the workpiece to be deformed according to the invention is advantageously in the form of a sheet, a tube, a profile, a wire, a joining rivet or any similar shape where it is possible to achieve by deforming with the TWIP effect a local setting of mechanical-technological values depending on the deformation level or the deformation degree. For instance, hardness and strength of the steel are increased by means of the method of the present invention.
  • the steel in connection with the TWIP effect during the deformation can also utilize the TRIP (Transformation induced plasticity) effect which is based on the transformation of the austenite to the martensite phase.
  • TRIP Transformation induced plasticity
  • This TRIP effect is dependent on the stacking fault energy.
  • the stacking fault energy is at the range of 18-20 mJ/m 2 the TRIP effect can exist during the deformation in which case some austenite will be transformed to martensite, but also in that case the main part of austenite will be under the TWIP effect without any phase transformation.
  • the deformation of the workpiece according to the invention can be carried out with essentially all common deforming processes.
  • Pressure deforming processes such as rolling, impression, pressing, punching, cutting, stamping or jacking are suitable for the method of the invention as well as push-pull forming processes such as deep-drawing, cupping, hydroforming, high pressure forming, collar forming or bulging.
  • Tensile forming processes such as embossing and bent forming processes such as bending, curling, seal curling, or bending by buckling can be utilized.
  • special forming processes such as shear forming, surface distortion or explosive forming are suitable.
  • joining processes which depends on forming like clincing or riveting, are possible to utilize with the present invention.
  • the workpiece during the deformation of the present invention is deformed to a form or geometry desired for the component based on the use of the component function.
  • Typical forms can be crimps, feather edges, foldings, press cuts and cut edges.
  • the form or geometry of the component can also be chosen so that the component can be mechanically joined with another component in an advantageous manner.
  • the deformation of the workpiece to a desired component according to the invention is carried out at the temperature range 0-400° C., preferably 20-80° C.
  • the component deformed according to the present invention can be applied for transport systems, such as cars, trucks, busses, railway or agricultural vehicles, as well as for automotive industry, and further in building and steel constructions, such as floor panels.
  • the component can be used for instance as
  • the component manufactured by the method of the present invention it is possible to control the intrusion during a crash as a material property by defining the region of the component based on the fact where ductile and where hardened areas are necessary.
  • FIG. 1 shows one embodiment of the invention for a component applied as an automotive b-pillar
  • FIG. 2 shows the results based on tension strength measurements in the regions of the component according to FIG. 1 .
  • an automotive b-pillar 1 is made of an austenitic TWIP steel sheet in 1.0 mm uniform thickness and containing 0.08 weight % carbon, 21 weight % manganese, 13 weight % chromium, less than 0.5 weight % nickel and 0.40-0.45 weight % nitrogen.
  • the b-pillar 1 is deformed so that there are four regions A, B, C and D having deforming degrees of 30%, 30-35%, 7% and 15% respectively.
  • FIG. 2 illustrates the tensile strength values in each measurement points 1-24 of the b-pillar 1. As a result it is shown that the regions with a higher deformation degree have a higher tensile strength.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Combustion & Propulsion (AREA)
  • Transportation (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Structural Engineering (AREA)
  • Architecture (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Articles (AREA)
  • Heat Treatment Of Sheet Steel (AREA)

Abstract

The invention relates to a method for manufacturing a component made of austenitic manganese alloyed steel using transformation induced plasticity. The component is deformed so that the component has an essentially same thickness of 0.5-2 millimeter in each region of the component, and the component has at least two regions having different mechanical property values.

Description

  • The present invention relates to a method for manufacturing a component made of austenitic manganese alloyed steel using the TWIP (Twinning-Induced Plasticity) effect of the steel to achieve a component having an essentially same thickness for the whole component but having regions with different mechanical property values.
  • When manufacturing components for transport systems such as cars, trucks, busses, railway or agricultural vehicles austenitic or ferritic steels, realizing the TRIP (Transformation induced plasticity), are used. It is calculated how much strength and material thickness is needed to fulfil the safety requirements. But when there are areas of a component which have a higher thickness than required, it is described as “overdesigned”. Therefore it is used arrangements to have the right material at the right place. Such possibilities are called “multi-material design” or “Tailored products” like Tailored roll forming, Tailored tempering or Tailored welded blanks. This means actually that it is calculated with homogeneous material properties and therefore construct only with thicknesses or to put different materials and sheets together.
  • The US publication 2013048150 describes a method for producing a workpiece having properties which are adjustable across a wall or a strip thickness by a special decarburizing annealing process, using the TRIP hardening effect of a high-manganese alloyed steel.
  • The WO publication 2014180456 describes a method for producing with only one material, austenitic lightweight construction steel, a component which has different material properties. The core is reached by a specific forming, where the austenitic lightweight construction steel has a temperature-dependent transformation induced plasticity (TRIP) and/or twinning induced plasticity effect (TWIP) during transformation The component is made to obtain high toughness during a temperature 40-160° C. above the room temperature and to obtain high strength during the temperature −65° C. to 0° C. below the room temperature. A gryogenic treatment is described also in the US publication 2014328715 in a method for producing a TWIP and nano twinned austenitic stainless steel containing less than 0.018 wt % C, 0.25-0.75 wt % Si, 1.5-2 wt % Mn, 17.80-19.60 wt % Cr, 24.00-25.25 wt % Ni, 3.75-4.85 wt % Mo, 1.26-2.78 wt % Cu, 0.04-0.15 wt % N the rest being Fe and unavoidable impurities.
  • The TWIP (Twinning-Induced Plasticity) effect depends on the chemical composition, austenitic microstructure hardening effect and the stacking fault energy (20-30 mJ/m2). In the TWIP effect a large amount of deformation is driven by the formation of deformation twins. The twinning causes a high value of instantaneous hardening rate when the microstructure becomes finer and finer. The resultant twin boundaries act like grain boundaries and strengthen the steel. The hardening rate value increases to a value of 0.4 at an approximate engineering strain of 30% and then remains constant until both the uniform elongation and the total elongation reach 50%.
  • The method for manufacturing of steel grades having the TWIP effect with different chemical compositions is also described for instance in the CN publication 103556052, in the CN publication 102312158, in the EP publication 2649214, in the KR publication 20100028310 and in the KR publication 20100009222.
  • The WO publication 2014/097184 relates to a use of the austenitic stainless steel with TWIP effect containing in weight % 0.01-0.50% C, 0.001-0.5% Si, 6-12% Mn, 11-20% Cr, 0.01-6.0% Ni, 0.01-2.0% Mo, 0.01-2.0 Co, 0.01-6.0% Cu, 0.11-0.50% N, 0.001-0.5% Nb, 0.001-2.0% Al, the rest being Fe and unavoidable impurities, for manufacturing automobile components with complex geometry for energy absorption, structural reinforcements and/or applications by deep drawing wherein corrosion resistance is requested.
  • The prior art is concentrated to describe how to produce or manufacture a steel with a TWIP hardening effect and what is their specific chemical analysis for the steel. Even though the WO publication 2014/097184 just mentions the use of the steel for automotive components, the WO publication 2014/097184 does not describe how the components are manufactured using its austenitic stainless steel.
  • The object of the present invention is to eliminate drawbacks of the prior art and to establish a method for manufacturing a component made of austenitic manganese alloyed steel using the TWIP effect by forming of the semi-manufactured product having essentially the same thickness to a component with regions having different mechanical property values. The essential features of the present invention are enlisted in the appended claims.
  • According to the method of the present invention a workpiece made of manganese alloyed steel is deformed using the TWIP (Twinning-Induced Plasticity) effect of the steel to achieve a component with essentially the same thickness, the range of the uniform thickness being 0.5-2.0 millimeter but which component has at least two regions having different mechanical property values. The mechanical property values desired for each region are dependent on the deformation level or the deformation degree which is performed for the workpiece. Therefore, according to the invention it is possible to achieve regions in the component which regions have different behavior in point of for instance stiffness, energy absorption, crash resistance.
  • In the TWIP effect the level of hardening depends on the deforming degree or deforming level (natural strain) but is independent from the deforming process. Therefore, all forming processes according to DIN 8582 are possible
  • The workpiece to be deformed in the method of the present invention is made of austenitic steel having stacking fault energy at the range of 18-30 mJ/m2. The manganese content of the steel is 10-25 weight %, preferably 15-20 weight %. The steel advantageously contains interstitial disengaged nitrogen and carbon atoms so that the sum of the carbon content and the nitrogen content (C+N) is at least 0.4 weight %, but less than 1.2 weight %, and the steel advantageously can also contain more than 10.5 weight % chromium, being thus an austenitic stainless steel. In case the steel contains essential contents of at least one ferrite former, such as chromium, a compensation with the contents of the austenite formers, such as manganese, carbon, nitrogen, nickel or copper will be done in order to have a balanced and sole content of austenite in the microstructure of the steel.
  • The workpiece to be deformed according to the invention is advantageously in the form of a sheet, a tube, a profile, a wire, a joining rivet or any similar shape where it is possible to achieve by deforming with the TWIP effect a local setting of mechanical-technological values depending on the deformation level or the deformation degree. For instance, hardness and strength of the steel are increased by means of the method of the present invention.
  • As one embodiment of the present invention in connection with the TWIP effect during the deformation the steel can also utilize the TRIP (Transformation induced plasticity) effect which is based on the transformation of the austenite to the martensite phase. This TRIP effect is dependent on the stacking fault energy. When the stacking fault energy is at the range of 18-20 mJ/m2 the TRIP effect can exist during the deformation in which case some austenite will be transformed to martensite, but also in that case the main part of austenite will be under the TWIP effect without any phase transformation.
  • The deformation of the workpiece according to the invention can be carried out with essentially all common deforming processes. Pressure deforming processes such as rolling, impression, pressing, punching, cutting, stamping or jacking are suitable for the method of the invention as well as push-pull forming processes such as deep-drawing, cupping, hydroforming, high pressure forming, collar forming or bulging. Tensile forming processes such as embossing and bent forming processes such as bending, curling, seal curling, or bending by buckling can be utilized. Further, special forming processes such as shear forming, surface distortion or explosive forming are suitable. Furthermore joining processes, which depends on forming like clincing or riveting, are possible to utilize with the present invention.
  • The workpiece during the deformation of the present invention is deformed to a form or geometry desired for the component based on the use of the component function. Typical forms can be crimps, feather edges, foldings, press cuts and cut edges. The form or geometry of the component can also be chosen so that the component can be mechanically joined with another component in an advantageous manner.
  • The deformation of the workpiece to a desired component according to the invention is carried out at the temperature range 0-400° C., preferably 20-80° C.
  • The component deformed according to the present invention can be applied for transport systems, such as cars, trucks, busses, railway or agricultural vehicles, as well as for automotive industry, and further in building and steel constructions, such as floor panels.
  • The component can be used for instance as
      • a side wall, floor panel, roof, step plate or entrance component in a railway vehicle car,
      • a bumper, cross member, longitudinal member, front wall, wheelhouse, dashboard cowl, pillar, channel in a passenger car
      • formed sheets, tubes or profiles in agricultural machines, buses or trucks
  • Using the component manufactured by the method of the present invention it is possible to control the intrusion during a crash as a material property by defining the region of the component based on the fact where ductile and where hardened areas are necessary.
  • In accordance with the method of the present invention it is advantageous to go with a ductile and soft material into a forming tool and to get out a high strength component. Normally in the prior art when it is wanted to have a high strength component it has to go into a forming tool and to get out with the same high strength material. In that case there is a possibility of cracks generating on the surface of the material during the forming process, because the deforming 10 degree was too much for the material.
  • The present invention is illustrated in more details referring to the attached drawings where
  • FIG. 1 shows one embodiment of the invention for a component applied as an automotive b-pillar,
  • FIG. 2 shows the results based on tension strength measurements in the regions of the component according to FIG. 1.
    •
  • In FIG. 1 an automotive b-pillar 1 is made of an austenitic TWIP steel sheet in 1.0 mm uniform thickness and containing 0.08 weight % carbon, 21 weight % manganese, 13 weight % chromium, less than 0.5 weight % nickel and 0.40-0.45 weight % nitrogen. The b-pillar 1 is deformed so that there are four regions A, B, C and D having deforming degrees of 30%, 30-35%, 7% and 15% respectively. There are 5 measurement points (1-5) in the region A, 5 measurement points (6-10) in the region B, 7 measurement points (11-17) in the region C and 7 measurement points (18-24) in the region D.
  • FIG. 2 illustrates the tensile strength values in each measurement points 1-24 of the b-pillar 1. As a result it is shown that the regions with a higher deformation degree have a higher tensile strength.

Claims (15)

1. A method for manufacturing a component made of austenitic manganese alloyed steel using transformation induced plasticity (TWIP), wherein the component is deformed so that the component has an essentially same thickness in the range of 0.5-2 millimeter in each region of the component, and the component has at least two regions with different mechanical property values.
2. The method according to claim 1, wherein the mechanical property values obtained in each region of the component are dependent on the deformation degree.
3. The method according to claim 1, wherein the deformation is carried out in the temperature range 0-400.
4. The method according to claim 1, wherein the deformation is carried out by a pressure deforming process.
5. The method according to claim 1, wherein the deformation is carried out by a push-pull forming process.
6. The method according to claim 1, wherein the deformation is carried out by a tensile forming process.
7. The method according to claim 1, wherein the deformation is carried out by a bend forming process.
8. The method according to claim 1, wherein the austenitic steel to be deformed is in the form of a sheet, a tube, a profile, a wire, or a joining rivet.
9. The method according to claim 1, wherein the austenitic steel to be deformed contains 10-25 weight % manganese.
10. The method according to claim 1, wherein the sum of the carbon content and the nitrogen content (C+N) in the austenitic steel to be deformed is more than 0.4 weight %, but less than 1.2 weight %.
11. The method according to claim 1, wherein the austenitic steel to be deformed contains more than 10.5 weight % chromium.
12. The method according to claim 1, wherein the stacking fault energy of the austenitic steel to be deformed is in the range of 18-30 mJ/m2.
13. The method according to claim 1, wherein the stacking fault energy of the austenitic steel to be deformed is in the range of 18-20 mJ/m2 and transformation induced plasticity is utilized in the steel during the deformation in connection with winning induced plasticity.
14. The method according to claim 3, wherein the deformation is carried out in the temperature range 20-80° C.
15. The method according to claim 9, wherein the austenitic steel to be deformed contains 15-20 weight % manganese.
US15/575,541 2015-05-22 2016-05-23 Method for manufacturing a component made of austenitic steel Expired - Fee Related US10774395B2 (en)

Applications Claiming Priority (4)

Application Number Priority Date Filing Date Title
EP15168786.0A EP3095889A1 (en) 2015-05-22 2015-05-22 Method for manufacturing a component made of austenitic steel
EP15168786.0 2015-05-22
EP15168786 2015-05-22
PCT/EP2016/061560 WO2016188948A1 (en) 2015-05-22 2016-05-23 Method for manufacturing a component made of austenitic steel

Publications (2)

Publication Number Publication Date
US20180127844A1 true US20180127844A1 (en) 2018-05-10
US10774395B2 US10774395B2 (en) 2020-09-15

Family

ID=53276729

Family Applications (1)

Application Number Title Priority Date Filing Date
US15/575,541 Expired - Fee Related US10774395B2 (en) 2015-05-22 2016-05-23 Method for manufacturing a component made of austenitic steel

Country Status (13)

Country Link
US (1) US10774395B2 (en)
EP (1) EP3095889A1 (en)
JP (1) JP6857618B2 (en)
KR (1) KR20180009774A (en)
CN (1) CN107646054B (en)
AU (1) AU2016266685A1 (en)
BR (1) BR112017025032A2 (en)
CA (1) CA2986172A1 (en)
EA (1) EA201792306A1 (en)
MX (1) MX2017014865A (en)
MY (1) MY181089A (en)
PH (1) PH12017502096A1 (en)
WO (1) WO2016188948A1 (en)

Families Citing this family (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
RU2659542C2 (en) * 2016-12-09 2018-07-02 федеральное государственное бюджетное образовательное учреждение высшего образования "Уфимский государственный авиационный технический университет" Super-strong high-manganese steel obtained by a combination of strengthening mechanisms

Family Cites Families (31)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS60141823A (en) * 1983-12-27 1985-07-26 Kobe Steel Ltd Production of nonmagnetic steel working member
JPH0619110B2 (en) * 1986-05-19 1994-03-16 株式会社神戸製鋼所 Method for producing high Mn austenitic stainless steel for cryogenic use
JP3384515B2 (en) * 1994-03-28 2003-03-10 日立金属株式会社 High thermal expansion steel and high strength high thermal expansion bolt
DE10259230B4 (en) * 2002-12-17 2005-04-14 Thyssenkrupp Stahl Ag Method for producing a steel product
FR2857980B1 (en) * 2003-07-22 2006-01-13 Usinor PROCESS FOR MANUFACTURING HIGH-STRENGTH FERRO-CARBON-MANGANESE AUSTENITIC STEEL SHEET, EXCELLENT TENACITY AND COLD SHAPINGABILITY, AND SHEETS THUS PRODUCED
US7806165B2 (en) * 2003-12-23 2010-10-05 Salzgitter Flachstahl Gmbh Method for making hot strips of lightweight construction steel
DE102004054444B3 (en) 2004-08-10 2006-01-19 Daimlerchrysler Ag Method for making steel articles with high rigidity and plasticity comprises mechanical shaping of steel in which twinning induce plasticity or shearband induced plasticity is produced, to give increase in rigidity of at least 30 percent
CN101065503A (en) * 2004-11-03 2007-10-31 蒂森克虏伯钢铁股份公司 High-strength steel strip or sheet exhibiting twip properties and method for producing said strip by direct strip casting
EP1846584B2 (en) * 2005-02-02 2022-12-14 Tata Steel IJmuiden B.V. Austenitic steel having high strength and formability method of producing said steel and use thereof
DE102008005803A1 (en) * 2008-01-17 2009-07-23 Technische Universität Bergakademie Freiberg Component used for armoring vehicles and in installations and components for transporting and recovering gases at low temperature is made from a high carbon-containing austenitic cryogenic steel cast mold
EP2090668A1 (en) * 2008-01-30 2009-08-19 Corus Staal BV Method of producing a high strength steel and high strength steel produced thereby
ES2705203T3 (en) * 2008-01-30 2019-03-22 Tata Steel Ijmuiden Bv Method to produce a hot-rolled TWIP steel and a TWIP steel product produced in this way
KR101020546B1 (en) 2008-07-18 2011-03-09 현대자동차주식회사 Ultra high strength TPI steel plate and its manufacturing method
KR101054773B1 (en) 2008-09-04 2011-08-05 기아자동차주식회사 Manufacturing Method of TPI Type Ultra High Strength Steel Sheet
DE102009003598A1 (en) * 2009-03-10 2010-09-16 Max-Planck-Institut Für Eisenforschung GmbH Corrosion-resistant austenitic steel
JP4984272B2 (en) * 2009-08-26 2012-07-25 有限会社Ｔｋテクノコンサルティング Steel with excellent vibration damping performance, method for producing the same, and damping body including the steel
KR101360737B1 (en) 2009-12-28 2014-02-07 주식회사 포스코 High strength steel plate having excellent resistance to brittle crack initiation and method for manufacturing the same
DE102010034161B4 (en) 2010-03-16 2014-01-02 Salzgitter Flachstahl Gmbh Method for producing workpieces made of lightweight steel with material properties that can be adjusted via the wall thickness
JP2011214127A (en) * 2010-03-31 2011-10-27 Tk Techno Consulting:Kk Vibration-suppression/base-isolation damper device
IT1403129B1 (en) 2010-12-07 2013-10-04 Ct Sviluppo Materiali Spa PROCEDURE FOR THE PRODUCTION OF HIGH MANGANESE STEEL WITH MECHANICAL RESISTANCE AND HIGH FORMABILITY, AND STEEL SO OBTAINABLE.
CN102312158B (en) 2011-09-13 2013-11-20 上海交通大学 Nb, Ti alloyed low-carbon high-intensity high-plasticity TWIP steel and preparation method thereof
ES2503566T3 (en) 2011-09-29 2014-10-07 Sandvik Intellectual Property Ab Austenitic stainless steel TWIP and nano-duplicate and method to produce it
EP2676684B1 (en) * 2012-06-18 2015-01-07 Biotronik AG Cobalt alloy for medical implants and stent comprising the alloy
JP2014058736A (en) * 2012-09-18 2014-04-03 Tk Techno Consulting:Kk Parts feeder
DE102012111959A1 (en) * 2012-12-07 2014-06-12 Benteler Automobiltechnik Gmbh Method for producing a motor vehicle component and motor vehicle component
ITRM20120647A1 (en) * 2012-12-19 2014-06-20 Ct Sviluppo Materiali Spa AUSTENITIC STAINLESS STEEL WITH HIGH PLASTICITY INDUCED BY GEMINATION, PROCEDURE FOR ITS PRODUCTION, AND ITS USE IN THE MECHANICAL INDUSTRY.
US10214790B2 (en) 2013-05-06 2019-02-26 Salzgitter Flachstahl Gmbh Method for producing components from lightweight steel
EP3255170B1 (en) * 2013-08-14 2021-03-31 Posco Ultrahigh-strength steel sheet and manufacturing method therefor
CN103556052B (en) 2013-11-08 2015-11-18 武汉钢铁(集团)公司 Automotive high manganese steel and manufacture method thereof
CN104593675A (en) * 2015-02-06 2015-05-06 深圳市晶莱新材料科技有限公司 Preparation method of metal material with TWIP (twinning induced plasticity) and TRIP (transformation of retained austenite induced plasticity) effects
TR201808389T4 (en) * 2015-07-16 2018-07-23 Outokumpu Oy Method for the production of austenitic twip or trip / twip steel component.

Also Published As

Publication number Publication date
MX2017014865A (en) 2018-03-23
MY181089A (en) 2020-12-17
JP6857618B2 (en) 2021-04-14
AU2016266685A1 (en) 2017-12-07
WO2016188948A1 (en) 2016-12-01
CA2986172A1 (en) 2016-12-01
PH12017502096A1 (en) 2018-05-07
JP2018522137A (en) 2018-08-09
EA201792306A1 (en) 2018-06-29
KR20180009774A (en) 2018-01-29
EP3095889A1 (en) 2016-11-23
BR112017025032A2 (en) 2018-08-07
CN107646054A (en) 2018-01-30
CN107646054B (en) 2020-03-31
US10774395B2 (en) 2020-09-15

Similar Documents

Publication Publication Date Title
DE102007039998B4 (en) Armor for a vehicle
KR102491409B1 (en) Cold deformation method of austenitic steel
US11400690B2 (en) High performance press-hardened steel assembly
US10774395B2 (en) Method for manufacturing a component made of austenitic steel
US12241139B2 (en) Method for manufacturing an austenitic steel component and use of the component
US12110571B2 (en) Method for partial cold deformation of steel with homogeneous thickness
EP3243913A1 (en) Method for the production of motor vehicle components protected against corrosion
CN117568569A (en) Method for preparing high performance stamped hardened steel components

Legal Events

Date Code Title Description
FEPP Fee payment procedure

Free format text: ENTITY STATUS SET TO UNDISCOUNTED (ORIGINAL EVENT CODE: BIG.); ENTITY STATUS OF PATENT OWNER: LARGE ENTITY

STPP Information on status: patent application and granting procedure in general

Free format text: DOCKETED NEW CASE - READY FOR EXAMINATION

AS Assignment

Owner name: OUTOKUMPU OYJ, FINLAND

Free format text: ASSIGNMENT OF ASSIGNORS INTEREST;ASSIGNORS:FROEHLICH, THOMAS;LINDNER, STEFAN;REEL/FRAME:046711/0098

Effective date: 20170409

STPP Information on status: patent application and granting procedure in general

Free format text: NON FINAL ACTION MAILED

STPP Information on status: patent application and granting procedure in general

Free format text: RESPONSE TO NON-FINAL OFFICE ACTION ENTERED AND FORWARDED TO EXAMINER

ZAAA Notice of allowance and fees due

Free format text: ORIGINAL CODE: NOA

ZAAB Notice of allowance mailed

Free format text: ORIGINAL CODE: MN/=.

STPP Information on status: patent application and granting procedure in general

Free format text: PUBLICATIONS -- ISSUE FEE PAYMENT VERIFIED

STCF Information on status: patent grant

Free format text: PATENTED CASE

FEPP Fee payment procedure

Free format text: MAINTENANCE FEE REMINDER MAILED (ORIGINAL EVENT CODE: REM.); ENTITY STATUS OF PATENT OWNER: LARGE ENTITY

LAPS Lapse for failure to pay maintenance fees

Free format text: PATENT EXPIRED FOR FAILURE TO PAY MAINTENANCE FEES (ORIGINAL EVENT CODE: EXP.); ENTITY STATUS OF PATENT OWNER: LARGE ENTITY

STCH Information on status: patent discontinuation

Free format text: PATENT EXPIRED DUE TO NONPAYMENT OF MAINTENANCE FEES UNDER 37 CFR 1.362

FP Lapsed due to failure to pay maintenance fee

Effective date: 20240915